REDUCTIVE BORON NITRIDE WITH EXTENDED REACTIVE VACANCIES FOR CATALYTIC APPLICATIONS

Abstract

A group of reductive 2D materials (R2D) with extended reactive vacancies and a method for making the R2D with extended reactive vacancies are provided, especially the example of the reductive boron nitride (RBN). To create defects such as vacancies, boron nitride (BN) powders are milled at cryogenic temperatures. Vacancies are produced by milling, and the vacancies can be used to reduce various metal nanostructures on RBN. Due to the thermal stability of the RBN and the enhanced catalytic performance of metal nanostructures, RBN-metals can be used for different catalysts, including electrochemical catalysts and high temperature catalysts.

Claims

1. A reductive boron nitride (RBN), wherein the RBN is a defective hexagonal boron nitride with chemical reactive sites that are randomly distributed on its surface, and wherein the chemical reactive sites are configured for reducing metal compounds or single metal atoms to their lower oxidation states.

2. The RBN of claim 1, wherein the metal compounds and metal atoms comprise Pt, Au, Ag, Pd, Fe, Co, and Ni, and any combination thereof.

3. The RBN of claim 1, wherein the chemical reactive sites are lattice imperfections.

4. The RBN of claim 3, wherein the lattice imperfections are extended reactive vacancies or reactive edges.

5. The RBN of claim 1, wherein the chemical reactive sites have reactive edges, and wherein the average lateral size of the reactive edges is from 400 μm to 10 micrometers.

6. The RBN of claim 1, wherein the chemical reactive sites have extended reactive vacancies, and wherein the average diameter of the extended reactive vacancies is from 170 μm to 50 nm.

7. The RBN of claim 1, wherein the chemical reactive sites have extended reactive vacancies, and wherein the extended reactive vacancies are configured for reducing the bandgap of hexagonal boron nitride (hBN) from insulating boron nitride (BN) to semiconducting RBN.

8. The RBN of claim 7, wherein the bandgap of the insulating BN is from 5 to 6 eV, and the bandgap of the semiconducting RBN is from 0.1 to 4.99 eV.

9. The RBN of claim 1, wherein the chemical reactive sites have extended reactive vacancies, and wherein the extended reactive vacancies are configured for emitting photons with energies ranging from 315 nm to 1400 nm.

10. The RBN of claim 1, wherein the average particle size of the RBN is less than 10 μm, and the surface area of the RBN is greater than 30 m.sup.2/g.

11. The RBN of claim 1, wherein the extended reactive vacancies are configured to reduce and anchor metal atoms and metal compounds in/on the RBN lattice to form a metal nanostructure decorated RBN.

12. The metal nanostructure-decorated RBN of claim 11, wherein the metal nanostructure decorated RBN comprises an isolated single atom, few-atom clusters with an average size ranging from 175 μm to 1 nm, nanoparticles with an average size ranging from 1 nm to 500 nm, and any combination thereof.

13. The metal nanostructure decorated RBN of claim 11, wherein the metal atom is used in a catalytic application, wherein the catalytic application comprises a hydrogen evolution reaction, an oxygen evolution reaction, an oxygen reduction reaction, an acetylene cyclotrimerization, a HCHO oxidation, a methanol oxidation, a CO oxidation, CO.sub.2 methanation, and a CO.sub.2 reduction.

14. A method for making reductive boron nitride (RBN) with extended reactive vacancies comprising mechanical grinding of hexagonal boron nitride at a cryogenic temperature to create extended reactive vacancies.

15. The method of claim 14, wherein the grinding time is longer than 0 min.

16. The method of claim 14, wherein the cryogenic temperature is at or below 123 K.

17. The method of claim 14, wherein the mechanical grinding is conducted in containers with one or more movable impactors.

18. A method for making metal nanostructure decorated reductive boron nitride (RBN) comprising: a) mixing RBN, wherein the RBN comprises extended reactive vacancies, with a metal precursor in a polar or non-polar solvent or solvents at room temperature; b) washing away excess metal compounds with polar or non-polar solvent or solvents by centrifugation or filtration; and c) re-dispersing materials obtained from b) in polar or non-polar solvent or solvents, wherein obtained liquid suspensions is used as is or as powders after evaporating the solvent or solvents.

19. The method of claim 18, wherein the metal is selected from all metals, and any combination thereof.

20. The method of claim 18, wherein the metals are in ionic form, and wherein the ionic form comprises Ag.sup.+, Pt.sup.4+, Au.sup.3+ in the obtained liquid suspensions.

21. The method of claim 18, wherein the solvent of the obtained liquid suspension is selected from the group consisting of polar and non-polar solvents, and wherein the solvent comprises ethanol, isopropanol, hexane, acetone, and any combination thereof.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0026] FIG. 1. (a) Schematic illustration of the synthesis of single atom Pt and few atoms AgPt clusters reduced on/by RBN. (b) The photograph of 500 mg hBN and RBN (90 and 900 min) after the reaction with 10 ml 0.001 M AgNO.sub.3 aqueous solution at room temperature. (c) HAADF-STEM image of single Pt atom on 90RBN (90RBN-Pt) with higher magnification. (d) Line profile from the white dashed line in (c).

[0027] FIG. 2. (a) XRD spectra of hBN and RBN with different cryo-milling time (90 and 900 min). (b) N.sub.2 adsorption and desorption isotherms of hBN, 90RBN, and 900RBN. (c-d) HRTEM image of the 90RBN, (c) showing the defects at the edges; (d) the triangular and point vacancies.

[0028] FIG. 3. Room-temperature photoluminescence spectra of 90RBN at 3 different sites with a 488 nm excitation laser. Emissions at 1.66, 1.75, 1.79, 1.82, 1.95, 2.05, and 2.10 eV can be found.

[0029] FIG. 4. (a) The HER polarization curves of 90RBN, 90RBN-Pt and 90RBN-Ag.sub.1Pt.sub.1. (b) Durability measurement of the 90RBN-Ag.sub.1Pt.sub.1. The polarization curves were recorded at the 1st cycle and after 10,000 cycles.

[0030] FIG. 5 HRSTEM images of (a) 90RBN-Ag, (b) 90RBN-Au, (c) 90RBN-Cu, (d) 90RBN-Fe, (e) 90RBN-CuPt, and (f) 90RBN-FePt.

[0031] FIG. 6. Thermal stability of 90RBN-Pt. Pt particle size distributions (up) and STEM images (down) of 90BN-Pt treated at different temperature in air. (a) room temperature, RT; (b) 200° C.; (c) 400° C.; (d) 600° C.

[0032] FIG. 7A. (a) HRSTEM images of RBN-NiPt; (b) CO.sub.2 conversion rate at different temperature with RBN-metal catalysts for the CO.sub.2 methanation reaction.

[0033] FIG. 7B. HRTEM images of (a) RBN and (b) RBN-Au.

[0034] FIG. 8. (a) XRD diffraction pattern for the pristine WS.sub.2 and WS.sub.2 cryomilled samples. (b) WS.sub.2 particle size calculated by Scherrer equation. (c) WS.sub.2 dispersions in acetone prepared with the pristine WS.sub.2, and with the cryomilled samples for 15, 30, and 45 min after 2 h of sonication (0.8 mg/mL). At the right of each sample is the corresponding WS.sub.2 film deposited on a FTO electrode.

[0035] FIG. 9. XRD diffraction pattern for the pristine MoS.sub.2 and MoS.sub.2 cryomilled samples.

[0036] FIG. 10. (a) Raman spectra and the (b) XRD diffraction pattern of graphite, 1 h, 2 h, and 3 h cryo-milled graphite.

[0037] FIG. 11. Raman spectra of graphite, boron nitride, and graphite/BN mixture after 2 h cryo-milling.

[0038] FIG. 12. XRD diffraction pattern for cryomilled MoS.sub.2 and cryomilled MoS.sub.2/WS.sub.2 mixture

[0039] FIG. 13. Raman spectra of cryomilled MoS.sub.2 and cryomilled MoS.sub.2/WS.sub.2 mixture

[0040] FIG. 14. N.sub.2 adsorption and desorption isotherms of pristine and cryomilled MoS.sub.2

[0041] FIG. 15. HRTEM images of cryomilled MoS.sub.2/WS.sub.2 mixture

[0042] FIG. 16. (a) The HER polarization curves of cryomilled MoS.sub.2/WS.sub.2 mixture. (b) Tafel slope of cryomilled MoS.sub.2/WS.sub.2 mixture. (c) The HER polarization curves of cryomilled MoS.sub.2/WS.sub.2 mixture with Pt functionalization. (d) Tafel slope of cryomilled MoS.sub.2/WS.sub.2 mixture Pt functionalization.

DETAILED DESCRIPTION OF THE INVENTION

Definitions

[0043] While the terms used herein are believed to be well understood by one of ordinary skill in the art, definitions are set forth herein to facilitate explanation of the subject matter disclosed herein.

[0044] Unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which the subject matter disclosed herein belongs. Although any methods, devices, and materials similar or equivalent to those described herein can be used in the practice or testing of the presently disclosed subject matter, representative methods, devices, and materials are described herein.

[0045] The terms “a,” “an,” and “the” refer to “one or more” when used in this application, including the claims. The use of the word “a” or “an” when used in conjunction with the term “comprising” in the claims and/or the specification may mean “one,” but it is also consistent with the meaning of “one or more,” “at least one,” and “one or more than one.”

[0046] All references to singular characteristics or limitations of the present disclosure shall include the corresponding plural characteristic(s) or limitation(s) and vice versa, unless otherwise specified or clearly implied to the contrary by the context in which the reference is made.

[0047] All combinations of method or process steps as used herein can be performed in any order, unless otherwise specified or clearly implied to the contrary by the context in which the referenced combination is made.

[0048] The methods and devices of the present disclosure, including components thereof, can comprise, consist of, or consist essentially of the essential elements and limitations of the embodiments described herein, as well as any additional or optional components or limitations described herein or otherwise useful.

[0049] Unless otherwise indicated, all numbers expressing physical dimensions, quantities of ingredients, properties such as reaction conditions, and so forth used in the specification and claims are to be understood as being modified in all instances by the term “about”. Accordingly, unless indicated to the contrary, the numerical parameters set forth in this specification and claims are approximations that can vary depending upon the desired properties sought to be obtained by the presently disclosed subject matter.

[0050] As used herein, ranges can be expressed as from “about” one particular value, and/or to “about” another particular value. It is also understood that there are a number of values disclosed herein, and that each value is also herein disclosed as “about” that particular value in addition to the value itself. For example, if the value “10” is disclosed, then “about 10” is also disclosed. It is also understood that each unit between two particular units are also disclosed. For example, if 10 and 15 are disclosed, then 11, 12, 13, and 14 are also disclosed.

EXAMPLE 1

Reductive Boron Nitride with Spontaneously Reduced Pt/AgPt for HER Catalyst

[0051] In the present invention, two-dimensional (2D) boron nitride (BN) with mechanically activated defects was selected as an ideal support to spontaneously reduce Pt single atom and AgPt subnanoclusters. Although BN itself is rarely considered as a promising catalyst, its excellent chemical stability, high thermal conductivity, and large band gap of 5.5 eV make it a strong candidate as catalyst support under various harsh conditions (e.g., high temperature, acid, and base). By introducing defects such as vacancies and hetero-atoms, BN can be activated to reductive boron nitride (RBN) so that the optical bandgap is reduced, and various defect levels are created within the forbidden gap. An RBN is a defective hexagonal boron nitride with chemical reactive sites that are randomly distributed on the surface and are capable of reducing metal compounds to their lower oxidation states including but not limited to metallic clusters and single atoms.

[0052] To create defects, BN powders were cryo-milled at −196° C. for a certain time as shown in FIG. 1(a). A series of RBN with different cryo-milling time (90 and 900 min) were prepared. Then the reductive BN (RBN) was mixed with a various salt solution such as AgNO.sub.3 aqueous solution at room temperature. Due to the reduction of Ag nanoparticles by RBN, the color of the powder is changed into blue in 90RBN and brown in 900RBN as shown in FIG. 1(b). Besides reducing Ag nanoparticles by RBN, atomically dispersed Pt atoms can also be spontaneously reduced by RBN, when the salt was changed PtCl.sub.4. The line profile from the STEM image shown in FIG. 1(c-d) further confirms that single Pt atom with diameter 0.21 nm was reduced and embedded in BN lattice. Moreover, bimetallic AgPt subnanoclusters can also be reduced by RBN layer when switching the salt solution to the mixture of AgNO.sub.3 and PtCl.sub.4.

[0053] The reactivity from the RBN is attributed to the defects including edges and vacancies in RBN. The X-ray diffraction (XRD) in FIG. 2(a) shows a gradual disordering process when the cryo-milling time increases, as the BN (002) peak becomes weakened and broadened. As cryo-milling time increases, BN flakes were exfoliated by the shearing force from the milling, resulting in the decrease in the grain size and the particle size. Thus, more surfaces and edges were exposed, giving rise to the increase in the surface area. The N.sub.2 sorption isotherms of the Hbn and RBN (90RBN and 900RBN) shown in FIG. 2(b) are classified as type II, indicating macropore solids, which is similar as that of exfoliated graphite. As cryo-milling time increases, the Brunauer-Emmer-Teller (BET) surface area and total pore volume increase from 37 m.sup.2 g.sup.−1 and 100 mm.sup.3 g.sup.−1 in hBN to 234 m.sup.2 g.sup.−1 and 516 mm.sup.3 g.sup.−1 in 900RBN, respectively. Besides the exposure of surfaces and edges via the exfoliation and the formation of smaller particles, the impact of milling also results in disordered structures, including exposed edges (FIG. 2(c)), and vacancies (point and triangular vacancies, FIG. 2(d)).

[0054] The introduced vacancies are also responsible for the created defect levels between the valence and conduction band of BN, giving rise to various photon emissions ranging from 1.59 to 2.19 eV.sup.2. Room temperature photoluminescence spectra of 90RBN collected from 3 sites shown in FIG. 3 reveal the emissions at 1.66, 1.79, 1.82, 1.95, 2.05, and 2.10 eV. Among those, the most intense emission is at 1.95 eV in all three sites, and previous work has revealed that this emission is associated with the presence of nitrogen-vacancy along with a substitution of nitrogen at the boron site. The created defect states also enable the charge transfer between the defective BN and the cations from the aqueous solution, so that Ag and Pt can be spontaneously reduced on the defective sites.

[0055] By reducing atomically dispersed Pt atoms and AgPt subnanoclusters on RBN, the compounds can be used as the catalyst for hydrogen evolution reaction (HER). The HER performance of RBN with atomically dispersed Pt and AgPt subnanoclusters (Ag.sub.1Pt.sub.1) was investigated in a 0.5 M H.sub.2SO.sub.4 solution. For an efficient HER catalyst, a high turnover frequency (TOF) and exchange current, and a low Tafel slope and onset potential are needed. The 90RBN (shown in FIG. 4(a)) exhibits negligible performance compared to the electrodes with Pt, indicating that only the atomically dispersed Pt atoms are HER active. In 90RBN-Pt where Pt atoms are atomically dispersed on BN, the onset potential is 82.5 mV that is comparable to commercialized Pt/C, and the Tafel slope is 51.4 mV dec.sup.−1. Normally, the HER on Pt surface undergoes the Volmer-Tafel reaction such that the rate-limiting step is the recombination step. However, in 90RBN-Pt, since single Pt atoms are isolated by inert BN, the recombination of chemisorbed hydrogen atoms becomes sluggish, resulting in a relatively higher Tafel slope in 90RBN-Pt compared to that of commercialized Pt/C. The HER performance can be improved by forming bimetallic AgPt subnanoclusters. When the Ag to Pt molar ratio is 1 to 1 (90RBN-Ag.sub.1Pt.sub.1), the best HER performance can be achieved with an onset potential of 30.2 mV and a Tafel slope of 33.2 mV dec.sup.−1. The exchange current of atomically dispersed Pt is 2 to 3 times higher than that of Pt in bulk form. TOF and exchange current reveal the intrinsic electrocatalytic activity per Pt atoms and the rate of hydrogen evolution per surface area at equilibrium, respectively. Hence, the improvements in TOFs and exchange current over Pt-based SACs further imply that the single atom catalyst (SAC) is designed to maximize the utilization of each metal atom which is counted as the active site, resulting in cost efficiency. The lifetime of the best performing catalyst 90RBN-Ag.sub.1Pt.sub.1 was evaluated in FIG. 4(b). FIG. 4(b) demonstrates that after 10,000 cycles the performance is comparable to that of the 1st cycle, indicating that AgPt clusters are robustly anchored on defective BN.

EXAMPLE 2

Other Metal Reduction Using Reductive Boron Nitride (RBN)

[0056] To reduce other metals, RBN powders were mixed with different aqueous solutions of metal precursors to reduce different metals into single atom and/or nanoclusters. In particular, 90RBN were mixed with AgNO.sub.3, FeCl.sub.3, CuSO.sub.4, and HAuCl.sub.4 to obtain Ag, Fe, Cu, and Au, respectively. As seen in FIG. 5, part (a), Ag were reduced into ˜8 nm nanoparticles on RBN. Similar trends are observed for reductions of Au, Cu, and Fe (FIG. 5, parts (b-d)). For Au, Cu, and Fe reduction; nanoclusters were formed with diameters ranging from 2-4 nm were identified by STEM (FIG. 5, parts (b-d)). In addition, bi-metallic nanoclusters, CuPt (FIG. 5 part (e)) and FePt (FIG. 5, part (f)), with atomically dispersed Pt atoms can also be reduced on 90RBN by mixing the precursors of Cu or Fe with Pt. The bi-metallic nanoclusters have the potential to work as the co-catalyst for reaction involving different reactants.

[0057] An advantage of using RBN as the metal support is that metals are reduced and confined at the vacancy sites, while the non-defect region still takes the advantage of the inert and thermally stable hBN. Ex-situ STEM experiments and statistical analysis were conducted using 90RBN-Pt with annealing temperature ranging from room temperature to 600° C. The majority of Pt atoms are single atoms until 200° C. (FIG. 6, parts (a, b)). Surprisingly, when the annealing temperature reached 400° C., more than 90% of the Pt atoms are still single atoms, although Pt atoms start to migrate and form larger particles (FIG. 6, part(c)). Only when the temperature reached 600° C., the majority of the Pt atoms coalesced into larger nanoparticles with an average diameter of 3.3 nm (FIG. 6, part (d)). Therefore, the formation of metal/RBN architectures at room temperature provides economical and scalable routes to synthesize thermally stable single metal catalysts (SAC) up to 400° C.

[0058] Due to the capability of reducing metal ions into nanostructures and the thermal stability to avoid metal aggregation, the RBN-metal composites can be further used as the high temperature catalyst, such as CO.sub.2 methanation. As seen in FIG. 7A, part (a), RBN-NiPt with atomically dispersed Pt atoms and ˜2 nm Ni clusters were reduced on RBN. By varying the ratio of NiPt, RBN-NiPt shows varied performance in converting CO.sub.2 into CH.sub.4. As seen in FIG. 7A, part (b), when the NiPt ratio is 1:1, the catalyst has the highest CO.sub.2 conversion rate of 50% at 500° C. These results further confirmed the possibility in using RBN-metal for high temperature (>100° C.) catalysts.

[0059] FIG. 7B shows results of a trial involving spontaneous reduction of Au nanoparticles on RBN, in which a Au(I) solution was first prepared by mixing 0.5 mL 0.01 M Au(III) tetrachloroaurate with 50 μL 0.005 M ascorbic acid and 9.45 mL DI water to form a colorless solution. Then, RBN was added into the prepared Au(I) solution. After a 10 min stirring, the solids were separated by centrifugation, followed by DI water washing and drying. The dried powder was characterized by high-resolution transmission electron microscopy (HRTEM). As shown in FIG. 7B, Au particles with a diameter ˜2-3 nm were spontaneously reduced on RBN, especially on the defective sites.

EXAMPLE 3

Defective WS.SUB.2 .Via Cryo-Milling

[0060] WS.sub.2 (2 μm, 99%, Sigma-Aldrich) was milled in a solid state at a cryogenic temperature (˜77.2 K) in a cryogenic mill SPEX 6770 Freezer/Mill. The cryogenic grinding process consisted of an oscillating steel impactor within a plastic vial, immersed in liquid nitrogen. Prior to the grinding process, each sample was pre-cooled for 10 minutes, and then cryo-milled with different time/cycles (10. 30. 45 min). Each milling cycle corresponds to 3 min grinding followed by 2 min of cooling.

[0061] After cryomilling, the samples were characterized by XRD. In FIG. 8(a) is shown an analysis of (002) peak, where the full width at half maximum (FWHM) of the normalized peak for the four samples was calculated. The peak area decrement for the longer cryomilled samples is related to the lattice deformation caused by atomic defects such as vacancies, dislocations, interstitial or substitutional atoms, and other defects caused by the cryomilling process. FIG. 8(b) presents the particle size obtained from calculations by the Scherrer equation and the corresponding FWHM (°) and milling time. The values indicate that cryomilling WS.sub.2 powder for 45 min reduces approximately 40% its particle size.

[0062] Due to the lattice deformation and grain size reduction, cryo-milled WS.sub.2 is easier to be dispersed in solution. Acetone dispersions of pristine WS.sub.2, 15WS.sub.2, 30WS.sub.2 and 45WS.sub.2 (0.8 mg/mL) were prepared from the cryomilled powder by placing them under sonication for two hours and then pouring them into a 6 cm.sup.3 cell leaving an electrode gap of 1 cm. The electrophoretic deposition was carried out by applying 60 V using a 2400 Keithley sourcemeter between two cleaned FTO on glass electrodes for 30 sec. The dispersions prepared with the samples milled for 15, 30 and 45 min have a difference in colloidal stability as compared to the dispersion prepared with pristine WS.sub.2. It is expected that, as the particle size decreases, the contribution of the Brownian motion plays a more important role in providing colloidal stability. FIG. 8(c) shows the resultant electrode after the electrophoretic deposition. The films show homogeneous deposition covering the substrate.

EXAMPLE 4

Defective MoS.SUB.2 .Via Cryo-Milling

[0063] Molybdenum disulfide (MoS.sub.2) is a layered semiconductive transition metal dichalcogenide (TMD). The XRD pattern of pristine MoS.sub.2 is characteristic for the hexagonal with the highest intensity reflection peak at d=6.16 Å (002) as disclosed in FIG. 9. After cryo-milling, no obvious phase change can be obtained, but defects, edges, and more exposed area are created in MoS.sub.2. After a 45 min cryo-milling, the grain size of MoS.sub.2 decreased to 48.6 nm from 77.2 nm in pristine MoS.sub.2. As shown in FIG. 14 cryo-milling time increases, the BET surface area and total pore volume increase from 10.9 m.sup.2/g and 38.2 mm.sup.3/gin pristine MoS.sub.2 to 24.8567 m.sup.2/g and 52.5 mm.sup.3 g.sup.−1 in 90 min MoS.sub.2, respectively. Due to the created defects, edges, and exposed edges, more dangling bonds are exposed as the reactive centers for molecular adsorption.

EXAMPLE 5

Defective Graphite Via Cryo-Milling

[0064] Graphite is a layered conducting material. Similar to BN, WS.sub.2, and MoS.sub.2, defects, edges, and exposed surfaces can be obtained by cryo-milling. As disclosed in FIG. 10(a), I.sub.D/I.sub.G gradually increases as cryo-milling time increase, indicating an increased amount of the induced structural disorder via cryo-milling. The gradual shifts in 002 peak (see FIG. 10(b)) as cryo-milling time increases suggests the expanded layer distance after cryo-milling.

EXAMPLE 6

Defective Graphite Via Cryo-Milling

[0065] The method can also be extended to the mixture of different 2D materials, for example, graphite and boron nitride mixture. Boron nitride and graphite were mixed before the cryo-milling. After 2 h cryo-milling, the mixture was well mixed, and defects were created. As disclosed in FIG. 11, Raman indicates the coexistence of boron nitride and graphite. In addition, the peak broadening implies that defects are presented in the mixture after the 2 h cryo-milling.

[0066] Although the present invention has been described in terms of specific exemplary embodiments and examples, it will be appreciated that the embodiments disclosed herein are for illustrative purposes only and various modifications and alterations might be made by those skilled in the art without departing from the spirit and scope of the invention as set forth in the following claims.

[0067] Documents reported herein are incorporated by reference in their entirety and do not carry an admission that they are prior art for any purpose. Where information specifically stated in this specification can be construed to contradict anything in the incorporated material, the information specifically stated in this specification shall control.

EXAMPLE 7

Defective MoS.SUB.2 .and WS.SUB.2 .Mixture Via Cryo-Milling for HER Catalyst

[0068] MoS.sub.2 and WS.sub.2 powders were also cryomilled together to form defective MoS.sub.2 and WS.sub.2 mixture. After 15-60 min cryo-milling, the powders were well mixed and defective. As seen in FIG. 15, many step edges and defective sites are formed after 60 min cryo-milling. Raman spectra was also applied to study the mixture and FIG. 13 shows the co-existence of both MoS.sub.2 and WS.sub.2. Similar effect is also shown on the XRD spectra of MoS.sub.2/WS.sub.2 mixture shown in FIG. 12. The defective sites in the mixture has also led to the enhanced HER catalytic performance. FIGS. 16 (a) and (b) shows the onset potential and Tafel slope of the cryo-milled mixture. The cryo-milling has also increased the chemical reactivity of the mixture which enables the mixture to spontaneous reduce PtCl.sub.4 into Pt clusters which shows enhanced HER performances shown in FIGS. 16 (c) and (d).